JPS63111128A - Manufacture of high tension high carbon steel wire rod having superior drawability - Google Patents

Manufacture of high tension high carbon steel wire rod having superior drawability

Info

Publication number
JPS63111128A
JPS63111128A JP25948786A JP25948786A JPS63111128A JP S63111128 A JPS63111128 A JP S63111128A JP 25948786 A JP25948786 A JP 25948786A JP 25948786 A JP25948786 A JP 25948786A JP S63111128 A JPS63111128 A JP S63111128A
Authority
JP
Japan
Prior art keywords
wire
steel
wire rod
strength
carbon steel
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
JP25948786A
Other languages
Japanese (ja)
Inventor
Toshio Fujita
利夫 藤田
Nobuhisa Tabata
田畑 綽久
Kimio Mine
峰 公雄
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
Kawasaki Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Kawasaki Steel Corp filed Critical Kawasaki Steel Corp
Priority to JP25948786A priority Critical patent/JPS63111128A/en
Publication of JPS63111128A publication Critical patent/JPS63111128A/en
Pending legal-status Critical Current

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Classifications

    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)

Abstract

PURPOSE:To prevent cup fracture due to central segregation and to improve the strength and ductility by adding a specified amt. of V to a steel having a specified compsn. contg. regulated amts. of Cr and Si and capable of being cold drawn without reheating. CONSTITUTION:A steel consisting of, by weight, 0.5-0.9% C, 0.3-0.6% Si, 0.4-0.9% Mn, 0.02-0.20% V, 0.03-0.10% Cr and the balance Fe is hot rolled to a wire rod and this wire rod is coiled in the form of a ring and subjected to direct controlled cooling by blast. Even when lead patenting by reheating is omitted, the wire rod can be drawn and cup fracture is not caused during drawing. In the steel, V has a strength and ductility improving effect but <0.02% V does not produce the effect. In case of >0.20% V, the effect is not further enhanced and the cost is increased, so the amt. of V in the steel is restricted to 0.02-0.20%.

Description

【発明の詳細な説明】 〔産業上の利用分野〕 本発明は伸線加工性に優れた高張力高炭素鋼線材の製造
方法に係り、特に再加熱処理を施すことなく冷間伸線が
可能な線材の製造方法に関し、PC鋼より線等の高強度
m線の製造の分野で利用される。
[Detailed Description of the Invention] [Field of Industrial Application] The present invention relates to a method for producing a high-strength, high-carbon steel wire rod with excellent wire drawability, and in particular allows cold wire drawing without reheating treatment. This method is used in the field of manufacturing high-strength m-wire such as PC steel stranded wire.

〔従来の技術〕[Conventional technology]

従来からJIS G3536のPC鋼線およびPC鋼よ
り線やJIS G3521の硬鋼線の如き高強度鋼線を
製造するには高炭素鋼線材を熱間圧延後に鉛パテンテイ
ングを施すことにより伸線加工性の良好なソルバイト組
織を得たのも更に最終製品の必要緒特性を満足させる方
法が採用されていた。
Conventionally, in order to manufacture high-strength steel wires such as JIS G3536 PC steel wire and PC steel stranded wire and JIS G3521 hard steel wire, high carbon steel wire rods are hot-rolled and then lead patented to improve wire drawability. In order to obtain a good sorbite structure, a method was adopted that also satisfied the required characteristics of the final product.

しかし、近年に至り、乙の鉛パテンテイングを省略し、
直接調整冷却処理した圧延のままの材料を伸線加工して
最終製品を得る方法が採られるようになってきた。しか
し最終製品の強度上昇の要求がますます高まっている。
However, in recent years, lead patenting has been omitted,
A method of obtaining a final product by wire-drawing as-rolled material that has been directly adjusted and cooled has come to be used. However, there is an increasing demand for increased strength in the final product.

従って素材の性質が最終製品の強度や延性もしくは伸線
過程のダイス寿命、伸線加工性自体に直接的影響を示す
ことになる。また、例えばPCfiより線の場合、伸線
加工度は大略85%で最終径は3〜5 mmとなり素材
径としては約8 in以上の大径サイズが対象となるの
が一般的である。
Therefore, the properties of the material directly affect the strength and ductility of the final product, the life of the die during the wire drawing process, and the wire drawability itself. For example, in the case of PCfi stranded wire, the degree of wire drawing is approximately 85%, the final diameter is 3 to 5 mm, and the material diameter is generally a large diameter size of about 8 inches or more.

「衝風調整冷却した時に強度不足が生じ易いこと」のた
めに、一般的に強度向上因子の一つである巻取温度を高
目に設定する等の対策がとられているが、この場合2次
スケール厚が厚くなりその脱落が生じ易くなって、需要
家で使用するまでに部分的に赤さびを生じ伸線前の酸洗
によっても剥離せずダイス寿命が低下することになる。
Generally speaking, countermeasures such as setting the winding temperature, which is one of the factors for improving strength, to a higher value are taken because "insufficient strength tends to occur during blast-controlled cooling," but in this case, The thicker the secondary scale becomes, the more likely it is to fall off, and by the time it is used by a consumer, it will partially develop red rust and will not peel off even when pickled before wire drawing, reducing the life of the die.

一方、鉛パテンテイングを施さずに冷間伸線する場合に
は、素材の中心偏析がその加工性阻害の大きな要因にな
ることも良く知られており、これを消去するために、素
材においてその拡散焼鈍を施すことが行われるが、その
熱処理費用は莫大である。また、強度を高める目的から
CやMnを増量することがあるが、これらの元素は偏析
元素であるため中心偏析の点からますます不利となる。
On the other hand, when cold wire drawing is performed without lead patenting, it is well known that center segregation of the material is a major factor that inhibits its workability. Annealing is performed, but the heat treatment cost is enormous. Further, the amount of C or Mn may be increased for the purpose of increasing the strength, but since these elements are segregated elements, this becomes increasingly disadvantageous in terms of center segregation.

また、本発明者らが先に開示した特開昭60−2631
に見られる如く化学成分を調整した鉛パテンテイングを
省略する方法が提案されており、これは主にCr、Si
の調整により必要強度を得ようとするものであるが、上
記の問題点を総合的には追求されておらず、この方法で
強度および延性改善を図るには限度がある。
In addition, the present inventors previously disclosed Japanese Patent Application Laid-Open No. 60-2631.
A method of omitting lead patenting by adjusting the chemical composition has been proposed, as seen in
However, the above-mentioned problems have not been comprehensively pursued, and there are limits to how much strength and ductility can be improved by this method.

〔発明が解決しようとする問題点〕[Problem that the invention seeks to solve]

本発明の目的は、上記従来技術の問題点を解決し、中心
偏析に起因するカッピー破壊を防止し、圧延のまま伸線
加工が可能な高強度鋼線用線材の製造方法を提供するに
ある。
An object of the present invention is to solve the above-mentioned problems of the prior art, to provide a method for manufacturing a wire rod for high-strength steel wire, which prevents cuppy fracture due to center segregation, and which allows wire drawing processing as it is rolled. .

〔問題点を解決するための手段および作用〕本発明の要
旨とするところは次の如くである。
[Means and operations for solving the problems] The gist of the present invention is as follows.

すなわち、重量比にて C:0.5〜0.9% Si:0.3〜0.6% Mn :  0.4〜0.9% V:  0.02〜0.20% Cr : 0.03〜0.10% を含み残部がFeおよび不可避的不純物から成る錆を線
材に熱間圧延した後リング状に巻取り衝風直接調整冷却
することを特徴とする、再加熱処理することなく伸線加
工性に優れた高張力高炭素鋼線材の製造方法である。
That is, in terms of weight ratio, C: 0.5-0.9% Si: 0.3-0.6% Mn: 0.4-0.9% V: 0.02-0.20% Cr: 0. 03 to 0.10%, with the balance consisting of Fe and unavoidable impurities, is hot-rolled into a wire rod, then wound into a ring shape and directly blast-controlled and cooled. This is a method for producing high-tensile, high-carbon steel wire with excellent wire workability.

まず、添加各元素は次のように調整する。First, each added element is adjusted as follows.

C: Cは熱間圧延後あるいは伸線加工後の強度および延性に
対して大きな影響を有する元素であり、上限値を09%
とする。その理由は、これを越えると中心偏析の程度が
顕著に悪化し、更に可塑性の低い初析セメンタイトを析
出するため伸線加工性が著しく阻害されるようになるか
らである。
C: C is an element that has a large effect on the strength and ductility after hot rolling or wire drawing, and the upper limit is 0.9%.
shall be. The reason for this is that if this value is exceeded, the degree of center segregation deteriorates significantly, and furthermore, pro-eutectoid cementite with low plasticity precipitates, which significantly impedes wire drawability.

一方、0.5%未満になると初析フェライト量が必然的
に多くなり必要強度が得られなくなるので下限を0.5
%とし、05〜0.9%の範囲に限定した。
On the other hand, if it is less than 0.5%, the amount of pro-eutectoid ferrite will inevitably increase and the required strength will not be obtained, so the lower limit is set to 0.5%.
%, and was limited to a range of 05 to 0.9%.

Sl: Siはマトリックスの固溶強化を図り9、強度、延性お
よびリラクセーション特性の改善に寄与する元素であり
、0.3〜06%の範囲に限定した。
Sl: Si is an element that aims at solid solution strengthening of the matrix and contributes to improving strength, ductility, and relaxation properties, and was limited to a range of 0.3 to 0.6%.

その限定理由は、Si量を変えた硬鋼線材5WRH,7
2A 、径5.5mmに80%の加工度を付与したもの
についてリラクセーション特性を調整したところ、第1
図に示す如くリラクセーション特性は03%を越えると
急激に改善されるようになり、0.6%になるとその効
果が飽和し、これを越又て添加する必要がないからであ
る。
The reason for this limitation is the hard steel wire 5WRH, 7 with a different amount of Si.
2A, when the relaxation characteristics were adjusted for a material with a diameter of 5.5 mm and a processing degree of 80%, the first
As shown in the figure, the relaxation properties are rapidly improved when the content exceeds 0.3%, and the effect is saturated when the content reaches 0.6%, so there is no need to add more than this.

M n : Mnも強度を確保する上で04%以上添加する必要があ
る。しかし、0.9%を越えると中心偏析の程度−が悪
化すると同時に、調整冷却中にマルテンサイト組織を発
生し、伸線加工性を大きく阻害するので09%以下に限
定した。
Mn: Mn must also be added in an amount of 0.4% or more to ensure strength. However, if it exceeds 0.9%, the degree of center segregation deteriorates, and at the same time, a martensitic structure is generated during conditioning cooling, which greatly impedes wire drawability, so it is limited to 0.9% or less.

V: ■は炭窒化物生成元素で、その析出強化作用を有するこ
とは主に中、低炭素鋼で良く知られているが、種々の研
究を重ねた結果、高炭素鋼に適用できることが判明し、
強度および延性の改善効果を有する。しかし、0,02
%未満ではその効果がなく、また、020%を越えても
その効果は飽和しコストも上るので002〜0゜20%
の範囲に限定した。
V: ■ is a carbonitride-forming element, and its precipitation-strengthening effect is well known mainly for medium- and low-carbon steels, but as a result of various studies, it was found that it can be applied to high-carbon steels. death,
It has the effect of improving strength and ductility. However, 0,02
If it is less than 0.0%, there is no effect, and if it exceeds 0.20%, the effect will be saturated and the cost will increase, so 0.02 to 0.20%.
limited to the range of

Cr: Crは焼入性向上元素であり、強度上昇に寄与するが、
他方、線材圧延後の2次スケールを堅固にする性質を併
せ有している。Crf!kを001〜0.10%範囲で
変化させた5WRH72Aを通常条件で圧延し、調整冷
却後、コイル外観から2次スケールの脱落状況を観察し
たところ、第2図に示す如く、Crが0.03%以上で
脱落は皆無となったので、Crの下限値を0.03%と
した。一方、強度の微調整も考慮して上限は0.10%
とした。
Cr: Cr is an element that improves hardenability and contributes to increasing strength, but
On the other hand, it also has the property of solidifying the secondary scale after rolling the wire rod. Crf! 5WRH72A with k varied in the range of 0.01 to 0.10% was rolled under normal conditions, and after adjusting and cooling, the falling off of secondary scale was observed from the appearance of the coil. As shown in Fig. 2, Cr was 0.1%. Since there was no dropout at 0.03% or more, the lower limit of Cr was set at 0.03%. On the other hand, the upper limit is 0.10% considering fine adjustment of strength.
And so.

本発明は上記限定成分の高炭素鋼を線材に圧延した後、
リング状に巻取り衝風直接調整冷却を行うのであるが、
その加熱、圧延、調整冷却条件は特に限定する必要なく
通常なされている条件で実施すればよい。かくして、本
発明法により製造した線材は再加熱処理を施すことなく
、冷間伸線加工を行うことができる。
In the present invention, after rolling the high carbon steel with the above-mentioned limited components into a wire rod,
It is wound into a ring shape and cooled by direct blast control.
The heating, rolling, and adjusted cooling conditions need not be particularly limited and may be carried out under commonly used conditions. Thus, the wire produced by the method of the present invention can be subjected to cold wire drawing without being subjected to reheating treatment.

〔実施例〕〔Example〕

具体的な実施例に基づいて更に詳細に説明する。 This will be explained in more detail based on specific examples.

第1表に化学成分を示した供試鋼を150胴角の鋼片と
した後、1150℃に加熱し径8IIII11および1
0mmに圧延した。線材仕上す214度は大略1050
〜1000℃であり、仕上り後直らに水冷帯を用い88
0〜900℃に急冷し、巻取りステルモア冷却装置で直
接調整冷却を施した。
The test steel whose chemical composition is shown in Table 1 was made into steel slabs with a body angle of 150 mm, and heated to 1150°C.
It was rolled to 0 mm. 214 degrees for wire finishing is approximately 1050 degrees
~1000℃, and immediately after finishing using a water cooling zone 88
It was rapidly cooled to 0-900°C and subjected to direct controlled cooling in a winding Stelmor cooling device.

圧延のままの線材の機械的性質およびミクロ組織を調査
しその結果を第2表に示17た。なお、ミクロ組織の特
性値としては3000倍の走査型電子顕微鏡で測定した
パーライトラメラ−間隔で示した。これが小さいほど伸
線加工性は良好である。
The mechanical properties and microstructure of the as-rolled wire were investigated and the results are shown in Table 2. The characteristic values of the microstructure are expressed as pearlite lamella spacing measured with a scanning electron microscope at 3000 times magnification. The smaller this value is, the better the wire drawability is.

比較fiA1、A2およびA3の強度および絞り値に比
較して本発明鋼はいずれも高い値を示し、ミクロ組織要
因のパーライトラメラ−間隔が細かくなっている。また
、本発明鋼は2次スケールの脱落が全くない。
Compared to the strength and reduction of area of comparative fiA1, A2, and A3, the steels of the present invention all exhibit higher values, and the pearlite lamella spacing, which is a microstructural factor, is finer. Further, the steel of the present invention has no secondary scale falling off.

比較鋼A1およびA2に比し、本発明鋼BあるいはC,
Dは強度が約8 kg f 7mm2上昇し、Si、C
rおよびVの効果が明らかである。また、比較鋼A3に
比しても本発明鋼E、F、、Gは同様の効果を発揮して
いる。一般的に強度の上昇、大径化は延性を劣化するが
、第2表に見る如く本発明鋼は比較鋼に比し優れており
、これらはパーライトラメラ−間隔の縮小に起因してい
る。更に中心偏析の影響が顕在化し易い比較fiA3に
は偏析部に若干の初析セメンタイトが認められたが、本
発明鋼のFおよびGには検出されず、加工性の良いこと
が推定される。
Compared to comparative steels A1 and A2, inventive steel B or C,
D has a strength increase of approximately 8 kg f 7 mm2, Si, C
The effects of r and V are obvious. In addition, the steels E, F, and G of the present invention exhibit similar effects compared to comparative steel A3. In general, increasing strength and increasing diameter deteriorate ductility, but as shown in Table 2, the steel of the present invention is superior to comparative steels, and this is due to the reduction in the pearlite lamella spacing. Furthermore, although some pro-eutectoid cementite was observed in the segregated areas in comparison fiA3, where the influence of center segregation is likely to become apparent, it was not detected in the invention steels F and G, suggesting that they have good workability.

次に伸線加工後の性質について説明する。第2表に示し
た線材について連続伸線機により伸線加工性を調べた。
Next, the properties after wire drawing will be explained. The wire rods shown in Table 2 were examined for wire drawability using a continuous wire drawing machine.

すなわち、最終線径における引張試験値、ダイス寿命お
よび伸線加工中の断線の有無を調査し、その結果を第3
表に示した。なお、前処理としては酸洗−ボラックス処
理を施し、総減面率は約83%を付与し、仕上伸線速度
は約350m/minとした。
In other words, the tensile test value at the final wire diameter, die life, and presence or absence of wire breakage during wire drawing were investigated, and the results were used in the third
Shown in the table. As a pretreatment, a pickling-borax treatment was performed to give a total area reduction rate of about 83%, and the final wire drawing speed was about 350 m/min.

第     3     表 比較fiA1、A2およびA3に比し、それぞれに対応
する本発明鋼は圧延のままの性質が受は継がれ、強度お
よび絞り値共にあきらかに高く、ダイス寿命も良好であ
る。また、初析セメンタイトの認められた比較#4A3
は伸線加工中にカッピー断線を生じたが、本発明鋼のF
、Gは全く支障を生じなかった。更に長さ300 m+
++の供試材を50本づつ連続サンプリングして引張試
験を行い、カッピー状破面の発生率を調査し、結果を第
4表に示した。カッピー破面率は次式により求めた。
Table 3 Comparison Compared to fiA1, A2, and A3, the corresponding steels of the present invention retain the as-rolled properties, are clearly higher in strength and reduction of area, and have good die life. Also, the recognized comparison of pro-eutectoid cementite #4A3
F of the steel of the present invention caused cuppy wire breakage during wire drawing.
, G caused no trouble at all. Furthermore, the length is 300 m+
Fifty specimens of ++ specimens were consecutively sampled and subjected to a tensile test to investigate the incidence of cuppy fracture surfaces, and the results are shown in Table 4. The cuppy fracture surface ratio was determined by the following formula.

カッピー破面率は、第4表に示す如(比較鋼については
CあるいはMn量が増えるに従って発生率が増加してい
るが、本発明鋼においては、C1Mnが高くなっても全
く発生していない。
The cuppy fracture rate is as shown in Table 4 (in the comparative steels, the rate increases as the C or Mn content increases, but in the steel of the present invention, no cuppy fractures occur at all even when the C1Mn content increases). .

更に、ブルーイング後にJIS G3536にょろりラ
クセーション試験を行い、その結果を同じく第4表に示
したが、本発明鋼は比較鋼に比し、十分に低い値を示し
優れていることば明らかである。
Furthermore, after bluing, a JIS G3536 Nyorori luxation test was conducted, and the results are also shown in Table 4, and it is clear that the steel of the present invention has a sufficiently lower value than the comparative steel, and is superior. .

〔発明の効果〕〔Effect of the invention〕

本発明は上記実施例からも明らかな如く、伸線加工後の
強度、延性、加工中の断線トラブルおよびダイス寿命等
を考慮してSi、Or、Vを微量添加する特定の関係の
下に成分を調整することによって、再加熱による鉛パテ
ンテイング処理を省略しても断線することなく伸線加工
が可能となり、かつ所期の諸特性を十分に満足する高強
度青線を製造でき、PC鋼より線等の製造コスト低減に
寄与するところ大である。
As is clear from the above examples, the present invention is based on a specific relationship in which Si, Or, and V are added in small amounts in consideration of strength and ductility after wire drawing, wire breakage problems during processing, die life, etc. By adjusting this, it is possible to draw the wire without breaking the wire even if the lead patenting treatment by reheating is omitted, and it is possible to produce a high-strength blue wire that fully satisfies the desired properties, making it possible to produce a high-strength blue wire that fully satisfies the desired properties. This greatly contributes to reducing manufacturing costs for wires, etc.

【図面の簡単な説明】[Brief explanation of the drawing]

第1図はSi含有量とりラクセーション値との関係を示
す線図、第2図はCr含有量と2次スケール脱落発生率
との関係を示す線図である。
FIG. 1 is a diagram showing the relationship between the Si content and the luxation value, and FIG. 2 is a diagram showing the relationship between the Cr content and the incidence of secondary scale shedding.

Claims (1)

【特許請求の範囲】[Claims] (1)重量比にて C:0.5〜0.9% Si:0.3〜0.6% Mn:0.4〜0.9% V:0.02〜0.20% Cr:0.03〜0.10% を含み残部がFeおよび不可避的不純物から成る鋼を線
材に熱間圧延した後リング状に巻取り衝風直接調整冷却
することを特徴とする、再加熱処理することなく伸線加
工性に優れた高張力高炭素鋼線材の製造方法。
(1) Weight ratio: C: 0.5-0.9% Si: 0.3-0.6% Mn: 0.4-0.9% V: 0.02-0.20% Cr: 0 .03 to 0.10%, with the balance consisting of Fe and unavoidable impurities, is hot-rolled into a wire rod, then wound into a ring shape, and directly blast-controlled and cooled, without any reheating treatment. A method for manufacturing high-tensile, high-carbon steel wire with excellent wire drawability.
JP25948786A 1986-10-30 1986-10-30 Manufacture of high tension high carbon steel wire rod having superior drawability Pending JPS63111128A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP25948786A JPS63111128A (en) 1986-10-30 1986-10-30 Manufacture of high tension high carbon steel wire rod having superior drawability

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP25948786A JPS63111128A (en) 1986-10-30 1986-10-30 Manufacture of high tension high carbon steel wire rod having superior drawability

Publications (1)

Publication Number Publication Date
JPS63111128A true JPS63111128A (en) 1988-05-16

Family

ID=17334766

Family Applications (1)

Application Number Title Priority Date Filing Date
JP25948786A Pending JPS63111128A (en) 1986-10-30 1986-10-30 Manufacture of high tension high carbon steel wire rod having superior drawability

Country Status (1)

Country Link
JP (1) JPS63111128A (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2658126A1 (en) * 1990-01-12 1991-08-16 Goodyear Tire & Rubber Assembly forming a bead core for a lorry tyre, lorry tyre comprising such an assembly and method for producing such an assembly
KR100368224B1 (en) * 1998-10-13 2003-03-17 주식회사 포스코 Manufacturing method of high strength steel for wire rod and wire rod with excellent freshness
KR100384629B1 (en) * 1998-10-16 2003-08-19 주식회사 포스코 A high strength wire-rod having superior wire drawability and a method therefor

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2658126A1 (en) * 1990-01-12 1991-08-16 Goodyear Tire & Rubber Assembly forming a bead core for a lorry tyre, lorry tyre comprising such an assembly and method for producing such an assembly
KR100368224B1 (en) * 1998-10-13 2003-03-17 주식회사 포스코 Manufacturing method of high strength steel for wire rod and wire rod with excellent freshness
KR100384629B1 (en) * 1998-10-16 2003-08-19 주식회사 포스코 A high strength wire-rod having superior wire drawability and a method therefor

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